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Mar 18, 2016 - Ionic Compatibilization of Cellulose Nanocrystals with Quaternary. Ammonium Salt and Their Melt Extrusion with Polypropylene...
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Ionic Compatibilization of Cellulose Nanocrystals with Quaternary Ammonium Salt and Their Melt Extrusion with Polypropylene Malladi Nagalakshmaiah,†,‡,§,∥ Nadia El Kissi,†,§ and Alain Dufresne*,‡,∥ †

LRP and ‡LGP2, Université Grenoble Alpes, F-38000 Grenoble, France § LRP and ∥LGP2, CNRS, F-38000, Grenoble, France S Supporting Information *

ABSTRACT: On account to their high mechanical properties along with high reinforcing capacity, cellulose nanocrystals (CNCs) could be the ultimate choice for polymer nanocomposites as filler. Recently, different strategies have been investigated for the melt extrusion of CNC-based polymer nanocomposites because it is a solvent-free process and because this technique is more viable for commercial industrialization. However, most thermoplastic polymers are processed at high temperatures, and sulfuric acid preparation of CNC limits the processing because of surface sulfate groups degradation. In this study we profitably used these negatively charged groups, and quaternary ammonium salt was ionically adsorbed on CNC by a simple aqueous method. Fourier transform infrared spectroscopy, thermogravimetric analysis, and X-ray diffraction were used to characterize adsorbed CNC, and changes in polarity were investigated by contact angle measurements. Modified CNC was extruded with polypropylene at 190 °C, and the ensuing composites were characterized in terms of mechanical (by dynamic mechanical analysis and tensile tests), thermal (by differential scanning calorimetry), and morphological (scanning electron microscopy) properties. The melt rheology of PP-based nanocomposites was also reported. KEYWORDS: cellulose nanocrystal, quaternary ammonium salt, polymer nanocomposite, melt extrusion, polypropylene

INTRODUCTION The use of nanomaterials as reinforcing phase into polymeric matrices to form nanocomposites has attracted attention because these materials generally display improved mechanical properties even at low filler content.1 Nanoreinforcing materials, such as hydroxyapatite,2 nano clays,3−7 carbon nanotubes,8−11 and reduced graphene oxide12 have been broadly studied. However, most of them are not biodegradable,1 and during the past decade, the interest for nanomaterials issued from renewable resources has increased. Cellulose nanocrystals (CNCs) extracted from natural plant fiber by strong acid hydrolysis are probably the most interesting nanomaterials for strengthening the properties of nanocomposites.13−15 However, the recent industrial-scale production of CNC at a commercial grade justifies the use of industrially scalable processes such as melt extrusion, which is the most common process to produce thermoplastic polymer composites. It is a highly viable and solvent-free process but relatively infrequent for the processing of polymer nanocomposites using CNC as the reinforcing phase. The main restrictions are related compatibility and thermal stability issues. Being highly hydrophilic, cellulose nanomaterials can form microscale aggregates when dried and/ or dispersed in a hydrophobic polymeric matrix. In addition, CNCs are classically prepared by a sulfuric acid hydrolysis treatment resulting in the formation of surface sulfate groups that are well-known to lower the thermal stability of the nanoparticles.16,17 These two factors limit the use of melt processing for the preparation of CNC reinforced nanocomposites, whereas © XXXX American Chemical Society

the solvent casting method was used in majority even if not wellsuited for industries.18 The surface functionalization of CNC is a possible solution to prevent microscale aggregation after drying as well in hydrophobic matrices.19−21 Toward the development of various applications, different approaches have been attempted to increase the dispersion of CNC in nonpolar matrices.22 It includes grafting of initiators for living radical polymerization,23−26 alkyne and azide groups,27,28 epoxy and amine groups,29 which can be further used for derivatization or click chemistry. The covalent bonding is typically directed by isocyanate reaction,30,31 acid halides,23,25,26 and acid anhydrides.32 The reaction medium usually consists of organic solvents requiring a previous solvent exchange step making this strategy hardly compatible with industrial environments.33 The aim of the present work was to implement a green and environmentally benign procedure consisting of aqueous-based surface modification using quaternary salts through strong electrostatic interactions. Few studies have been previously reported on surfactant modification of CNC, despite different purpose.34−37 Recently, investigation of CNC Pickering emulsions charged with surfactant was described.38 The preparation of surfactant-modified CNC reinforced polylactic acid (PLA) nanocomposites was also reported, but it was shown Received: February 7, 2016 Accepted: March 18, 2016


DOI: 10.1021/acsami.6b01650 ACS Appl. Mater. Interfaces XXXX, XXX, XXX−XXX

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ACS Applied Materials & Interfaces Scheme 1. Expected Reaction of the Quaternary Ammonium Salt with Cellulose Nanocrystals

Thermogravimetric Analysis. Thermal stability of the samples was monitored by TGA using a simultaneous thermal analyzer (STA) 6000 (PerkinElmer, USA). The weight loss and dTG curves were obtained for a 20 mg sample at a heating rate of 10 °C.min−1 in the temperature range of 30−950 °C under oxidizing atmosphere (air). X-ray Diffraction. Wide-angle XRD analysis was performed on dried CNC nanomaterials that were stored under controlled humidity (50% RH) and temperature (23 °C). A 2.5 mm deep cell was used for the analysis. Measurements were performed with a diffractometer (X′ Pert PROMPD, PAN analytical, Netherlands) attached to a detector. The operating conditions of the refractometer were: copper Kα radiation (λ = 1.5418 Å), 2θ (Bragg angle) between 2 and 56°, step size 0.067°, counting time 90 s. Each sample was measured once. Contact Angle Measurements. The hydrophilic/hydrophobic nature of unmodified and modified was evaluated at room temperature by measuring the contact angle of a small water drop (ca. 5 μL) using an Attension theta contact angle meter. Smooth surfaces were obtained by compacting freeze-dried CNC under a pressure of 10 MPa. Contact angle values were determined from Attension theta Software. Nanocomposite Processing. Extrusion was used to prepare PP nanocomposite films reinforced with various filler contents with a twinscrew DSM Micro 15 compounder. The polymer matrix (PP) and freeze-dried CNC were first mixed and introduced in the mixing chamber. Around 15 g of material was used, and the mixing conditions were 190 °C at 150 rpm for 8 min. Extrusion through a slit 0.6 mm wide and 1 cm long die was carried out. PP nanocomposites were prepared with modified CNC (M-CNC) at 1, 3, 6, and 10 wt %, and unmodified nanocrystals at 3 wt % were used to compare the results. Visible Light Transmittance. Shimadzu UV 2401 UV vis spectrometer was used to analyze the transmittance of the nanocomposite films within the range 200−800 nm. The transmittance spectra were acquired using air as background. The resolution of the spectrophotometer was 1.5 nm, and the photometric accuracy was ±0.01 in absorption. Dynamic Mechanical Analysis. The viscoelastic behavior of the nanocomposites was investigated by dynamic mechanical analysis (DMA). Experiments were carried out with a RSA3 (TA Instruments, USA) equipment working in tensile mode. The storage modulus E′ was recorded as a function of temperature while the material deformed under an isochronal oscillatory stress. Measurements were performed with a frequency of 1 Hz, from −30 to 100 °C with a ramp rate equal to 3 °C min−1. The length of the sample was 10 mm. Tensile Tests. The tensile high-strain mechanical tests were performed using a RSA3 (TA Instruments, USA) with a load cell of 100 N. Sample dimensions were 4−5 mm and 20 mm for width and length, respectively, and the gap between pneumatic jaws at the start of each test was adjusted to 10 mm. Before analysis the samples were stored overnight in desiccators containing silica gel. All experiments were carried out at room temperature (25 °C) with a cross-head speed of 3 mm min−1. Differential Scanning Calorimetry. Differential scanning calorimetry (DSC) was used to investigate the melting behavior of the nanocomposites. Measurements were performed with a PerkinElmer DSC instrument using aluminum pans. The samples were scanned from −30 to 200 °C at a heating rate of 10 °C min−1.

that the surfactant had a negative effect such as polymer chain degradation of the PLA.39 In the present study, a comprehensive investigation of surfactant-coated CNC-reinforced polypropylene composites prepared by melt extrusion was addressed. This type of material could find potential applications as automotive parts, sailing dinghies, packaging, etc. In order to strengthen the interactions between CNC and adsorbed molecules, the sulfate groups borne on CNCs were profitably used. Quaternary ammonium cations bearing long alkyl groups were used to modify the surface by a chemical-free method that is more compatible for industrial applications. The dispersibility of modified CNCs in organic solvents was studied, and their surface charge was measured. Atomic force microscopy (AFM), Fourier transform infrared spectroscopy (FTIR), X-ray diffraction (XRD), and thermogravimetric analysis (TGA) were used to characterize the nanomaterials. Contact angle measurements were employed for accessing hydrophobicity of the modified nanomaterial. The modified CNCs prepared by this water-based method were used for melt extrusion with high-molecular-weight polypropylene matrix. The ensuing nanocomposites were characterized in terms of thermal, mechanical, morphological, and rheological properties.


Materials. Sodium hydroxide (Sigma-Aldrich) and hexadecyl trimethylammonium bromide (Sigma-Aldrich) were used as received. Commercial grade cellulose nanocrystals (CNCs) were purchased from University of Maine, USA, as 11.5 wt % suspension. Elemental analysis showed that the sulfur content was 1.1 wt % and the surface half ester groups per 100 bulk glucose units was 5.65 considering C6H10O5-(SO3)n as the basic formula as described elsewhere.40 The surface charge density was −36.15 mV (Zetasizer measurement). The density and weightaverage molecular weight of polypropylene (PP) used as matrix in this study were 0.960 g cm−3 and 337 000 g·mol−1, respectively. Zeta Potential Measurements. The surface charge density was measured by using the Malvern Instruments Zetasizer ZEN-2600 zeta sizer. Data were averaged over 10 measurements. Atomic Force Microscopy. AFM observations were used to study the diameter and approximate length of individual nanocrystals using a Nanoscope III (Veeco, USA). CNC samples were previously diluted to a concentration of 0.01 wt %, and a drop of the suspension was placed on a mica plate and allowed to dry at room temperature overnight. Tapping mode and silicon cantilever (OTESPA, Bruker, USA) were used for the observations. At least 10 different locations were analyzed to obtain representative measurements. CNC diameter was determined from height profile of height sensor images. Fourier Transform Infrared Spectroscopy. FTIR analysis was done by means of a Spectrum 65 spectrometer (PerkinElmer, USA) on dried CNC obtained by freeze-drying for 24 h, in order to determine the functional groups borne by CNC. The samples were analyzed by attenuated total reflectance (ATR). B

DOI: 10.1021/acsami.6b01650 ACS Appl. Mater. Interfaces XXXX, XXX, XXX−XXX

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Figure 1. Wettability tests: (a) unmodified CNC and (b) CNC modified with quaternary ammonium salt (M-CNC) in a solvent system composed of chloroform (lower phase) and water (upper phase), and (c) M-CNC dispersed in toluene, ethyl acetate, and chloroform (from left to right).

Figure 2. AFM images for (a) unmodified CNC, (b) quaternary salt, and (c) modified CNC. Scanning Electron Microscopy. The nanocomposite cross section was observed by scanning electron microscopy (SEM) in order to check the possible filler aggregation. Samples were previously frozen using liquid nitrogen and broken to obtain a clear fracture. (The polymer was in the glassy state T ≪ Tg.) It was glued to the sample holder for cross section images. The samples were coated with gold in order to prevent the charring of the sample due to the electron bombardment. The SEM images were captured by using FEI (MED) Quanta200. Melt Rheology. A dynamic oscillatory rheometer was used to analyze the viscoelastic behavior of the nanocomposites in the melt state from 0.1 to 100 rad s−1. A controlled strain rheometer (ARES, Advanced Rheometric Expansion System, and Rheometric Scientific) fitted with 25 mm diameter parallel plate geometry was employed. Samples were directly loaded and molded between the plates. The tests were carried out at 180 °C with a gap distance of 1 mm under nitrogen atmosphere.

CNC dispersion was slowly added to the 500 mg of quaternary salt at 40 °C, i.e., the ratio of salt to CNC was 10 wt %. The mixture was stirred at 40 °C for 3 h, under constant temperature because the sulfate groups are sensitive to the alkali conditions at high temperatures. Then, the mixture was stirred at room temperature and dialyzed against deionized water for 2 weeks in order to remove unabsorbed QS and NaBr formed during reaction. The mixture was freeze-dried before extrusion with PP. Unmodified CNC and CNC modified with quaternary ammonium salt will be denoted as CNC and M-CNC, respectively. The surface charge of modified and unmodified CNC was measured and ζ potential values were determined. The surface charge of unmodified CNC was −36.15 mV because of the negatively charged sulfate groups induced by the sulfuric acid treatment.17 After surface modification, the CNC showed a +6.09 mV ζ potential value because the surface charge was neutralized by QS and the positive charge is due to the nonadsorbed quaternary salt. A simple and effective method to highlight the changes induced by the surface modification was conducted through wettability tests. After freeze-drying, the dialyzed final suspension of M-CNC was redispersed in different organic solvents such as toluene, chloroform, and ethyl acetate (1 wt %), and the dispersion was ultrasonicated for 1 min. Photographs of these suspensions can be seen in Figure 1. Figure 1a shows unmodified CNC in a solvent system composed of water and chloroform. These two liquids are immiscible, and the upper phase

RESULTS AND DISCUSSION In this section, the surface modification of CNC will be first described, and then the structural, functional, surface, and thermal properties for both modified and unmodified CNCs will be reported. Thereafter, the characterization of polypropylene composites reinforced with these cellulosic nanomaterials will be presented. As shown in Scheme 1, the quaternary ammonium salt (QS) hexadecyl trimethylammonium bromide was utilized to promote electrostatic interactions with CNC bearing sulfonated groups on their surface. A previously reported procedure was used.41 For this, 5 g of CNC were dispersed in aqueous medium (1 wt % in water), and the pH was adjusted to 10 by using NaoH. Then, the C

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ACS Applied Materials & Interfaces corresponds to water (density = 1 g cm−3) whereas the lower phase corresponds to chloroform (density = 1.49 g cm−3). It is clearly observed that unmodified CNC displays a higher affinity for water, which is a polar solvent, and migrates to the aqueous phase because of its hydrophilic nature. Figure 1b shows that on the contrary M-CNC migrates to the chloroform phase. Figure 1c shows M-CNC in toluene, ethyl acetate, and chloroform (from left to right). A good dispersion is observed indicating that the nanocrystal surface was less polar after chemical modification. Similar results were obtained in previous work.33,42 The structural morphology of modified and unmodified CNC was investigated by means of AFM. The CNCs used in this study were of commercial grade and produced from wood pulp. Figure 2a shows an AFM image of these CNCs. The length and diameter of the nanorods are within the range 24−195 and 2−9 nm, respectively. The modified CNCs can be seen in Figure 2c. The length and diameter of the M-CNC increased by 3−5 and 10 nm, respectively. It can be ascribed to the surface adsorption of the quaternary salt which size is around 2−8 nm as can be seen in Figure 2b. These values are consistent with surfactant layer 15 Å thick reported when coating CNC with phosphoric ester of poly(ethylene oxide) (9) nonyl phenyl.35 FTIR spectroscopy was used to check the functional properties of both neat and modified CNC. FTIR spectra obtained for neat CNC and M-CNC are shown in Figure 3.

bands at 2868 and 2970 cm−1, which correspond to asymmetric and symmetric −CH2− stretches from fatty chain, was observed.44 The signal at 1650 cm−1 is attributed to the vibration of adsorbed water, and it strongly decreased after modification, probably due of the more hydrophobic behavior of the modified nanomaterial and a new band at 1480 cm−1,33 attributed to the trimethyl groups of the quaternary ammonium can be identified for the modified CNC sample. The thermal stability of freeze-dried CNC and modified CNC was analyzed using TGA as shown in Figure 4. An initial weak weight loss was observed at lower temperatures for neat CNC, which was attributed to moisture removal. Then, a continuous weight loss was noted from 200 to 600 °C. This behavior was expected because of sulfate groups induced by the sulfuric hydrolysis treatment.16,17 The weight loss around 200 °C is related to more accessible sulfate groups in amorphous cellulose regions. The weight loss around 400−600 °C corresponds to the breakdown of unsulfated crystalline cellulose regions. The thermal stability is known to depend on the number of surface sulfate groups.45 For M-CNC, the thermal degradation behavior is significantly different, and the temperature values associated with different relative weight loss values for neat and modified CNC have been reported (Table 1). The low-temperatures weight loss is less Table 1. Weight Loss Values at Different Temperatures for Neat CNC and CNC Modified with Quaternary Ammonium Salt (M-CNC) temperature (°C) at different relative weight loss sample






227 292

238 303

271 314

426 361

pronounced for M-CNC compared to that for CNC. This is obviously due to the more hydrophobic nature of the material. Moreover, the degradation temperature is clearly shifted to higher temperatures for M-CNC compared to that of neat CNC, and this might be due to the strong electrostatic adsorption of QS on the surface of CNC and the long aliphatic chains of QS that cover the surface sulfate groups. It should help the processing of PP-nanocomposites when using M-CNC. Also, it is interesting to see that the char residue is lower for M-CNC than for CNC as

Figure 3. FTIR spectra obtained for neat CNC and CNC modified with quaternary ammonium salt (M-CNC).

Unmodified CNC displays several bands characteristic of cellulose at 3350 cm−1 (O−H) and 2868 and 2970 cm−1 (C− H from −CH2−). For M-CNC, a substantial increase of the

Figure 4. (a) TGA spectra and (b) dTG curves for unmodified CNC and CNC modified with quaternary ammonium salt bearing long alkyl chain (MCNC). D

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Figure 5. X-ray diffraction patterns obtained for unmodified CNC and CNC modified with quaternary ammonium salt bearing long alkyl chain (MCNC).

expected because it was shown that the char residue is increased when increasing the number of sulfate groups on nanocrystals.16 The relative dTG curves corresponding to CNC and M-CNC are shown in Figure 4b, and they clearly indicate that the main degradation temperature for CNC is lower than for M-CNC. It shows further that the surface of CNC is modified with the quaternary salt. The crystalline structure of CNC plays a vital role in their reinforcing effect, and it should be well-maintained even after modification. XRD was used to study the crystalline structure of CNC and M-CNC. The diffraction patterns for both modified and neat CNC are shown in Figure 5. The diffraction peaks appearing at 22.6, 14.8, 16.4, and 34.4° were related to the typical reflection planes of cellulose I.46,47 The intensity of the 16.4° peak was slightly increased (expanded view in Figure 5) after modification, which is due to the surfactant adsorption. This indicates that surface modification has no impact on the crystalline structure of modified cellulose nanocrystals and that surfactant modification is only on the surface of CNC as expected. The hydrophobic/hydrophilic nature of CNC was investigated using contact angle measurements. The results are presented in Figure 6. As expected, the contact angle value for modified CNC is higher than that for neat CNC. A sharp decrease of the contact angle of the water drop for unmodified CNC was observed with spreading within 30 s, and the contact angle after 20 s was around 20° (±2). Even after several measurements, the same behavior was always observed. This is obviously due to the hydrophilic nature of CNC, whereas MCNC has a significantly higher contact angle around 45° (±3) that remained constant even after 20 and 30 s. This is clear evidence of the hydrophobic nature induced by the surface modification. The −OH groups are hidden by the long fatty chains on the surface of the CNC as described in Scheme 1.

Figure 6. Evolution of the contact angle for a water drop vs time on sheet samples (inserted photographs for the water drop on the sheet sample after 5 and 20 s) for unmodified CNC and CNC modified with quaternary ammonium salt bearing long alkyl chain (M-CNC).

Nanocomposites were prepared by melt extrusion using PP as matrix and either unmodified or modified nanocrystals as the reinforcing phase. The aspect of resultant nanocomposite films is shown in Figure 7. The neat PP film is translucent as for any low thickness semicrystalline polymer film. When adding only 3 wt % unmodified CNC, the film becomes evenly darker. This is obviously due to the degradation of the nanofiller. The appearance of nanocomposite films reinforced with up to 10 wt % modified CNC is similar to the one of neat PP film. This observation agrees with TGA experiments, and this might be due to the protection of the sulfate groups on surface of CNC provided by the electrostatically interacting quaternary ammonium chains. Similar observations were reported when coating CNC with high-molecular-weight polyoxyethylene (PEO),18,48 E

DOI: 10.1021/acsami.6b01650 ACS Appl. Mater. Interfaces XXXX, XXX, XXX−XXX

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Figure 7. Appearance of extruded PP/CNC and M-CNC nanocomposite films: PP+10%M-CNC, PP+6%M-CNC, PP+3%M-CNC, PP+1%M-CNC, PP+3%CNC, and PP (from left to right).

but higher interactions are expected between negatively charged sulfated CNC and quaternary ammonium salt. The light transmittance of CNC and M-CNC extruded polypropylene nanocomposites was analyzed by UV spectrophotometer, as shown in Figure S1. It is observed that when adding CNC and M-CNCs to PP matrix the transmittance decreased particularly for composites containing higher filler contents. The PP matrix shows a high transmittance (65%) because subsequently it is transparent. The lowest transmittance (36.8%) was observed for the PP film reinforced with unmodified CNC (3 wt %) because of the degradation of the cellulosic nanomaterial as evidenced in Figure 7. However, this effect was alleviated when using up to 10 wt % modified CNC. The transmittance was around 60, 57.2, and 49.5% for PP films reinforced with 1, 3, and 6 wt % M-CNC, respectively. A stronger decrease of the transmittance to 40.5% was observed for the 10 wt % M-CNC reinforced composite and is probably due to the filler aggregation. Overall, the transmittance of M-CNC reinforced composites are higher than 40%. The thermal characterization of CNC/M-CNC-reinforced PP nanocomposite films was analyzed by DSC measurements. The thermograms can be seen in Figure S2, and they were used to determine the thermal data collected in Table 2. Neat PP displays a melting point around 170 °C that drops to 163 °C after extrusion. Moreover, an additional peak appears around 122 °C for extruded PP. Both events are brought about by the extrusion

process and could possibly be attributed to a decrease of the molecular weight of the polymer upon extrusion due to high shear rates involved during melt processing.49 This secondary melting peak progressively recedes when adding modified CNC, and it is absent for the nanocomposite film containing 3 wt % unmodified CNC. The melting temperature of PP does not show any significant change upon CNC loading. In contrast, the degree of crystallinity of the polymeric matrix tends to increase continuously when adding the cellulosic nanomaterial. It is noteworthy that for the calculation of the degree of crystallinity the enthalpy of fusion was normalized to account for the effective PP content. The CNC-induced crystallization and its nucleating effect have been abundantly reported for different polymer matrices. The mechanical properties nanocomposite films reinforced with CNC/M-CNC were investigated in both the linear and nonlinear range. The evolution of the logarithm of the storage tensile modulus (log E′) as a function of temperature in isochronal conditions for a frequency of 1 Hz is shown in Figure 8. The curves have been normalized at 1 GPa in the lowtemperature range to limit the effect of the errors induced by the measurement of the dimensions of the sample. For neat PP, the modulus gradually declines with increasing temperature from −30 to 100 °C. When adding 3 wt % unmodified CNC, a significant increase of the storage modulus is observed over the whole temperature range. Regarding modified CNC, a similar

Table 2. Melting Temperature (Tm), Enthalpy of Dusion (ΔHm) and Degree of Crystallinity (χc) for Neat PP, Extruded PP (PPex) and Nanocomposites sample

Tm (°C)

ΔHm (J g‑1)

χc (%)a

PP PPex PP+3% CNC PP+1% M-CNC PP+3% M-CNC PP+6% M-CNC PP+10% M-CNC

170.9 163.6 164.8 165.9 164.4 164.0 163.7

66.03 62.92 78.53 73.71 80.65 81.98 83.40

34.7 33.1 42.6 39.2 43.8 45.9 48.8


χc =

ΔHm w × ΔHm°

Figure 8. Evolution of log E′ as a function of temperature at 1 Hz for neat extruded PP (●) and nanocomposites reinforced with 3 wt % CNC (open red circles) and 1 wt % (solid blue circles), 3 wt % (solid red circles), 6 wt % (solid green circles), and 10 wt % M-CNC (solid orange circles).

where ΔH°m= 190 J g−1 is the enthalpy of fusion for 100% crystalline PP50and w is the weight fraction of PP matrix in the material. F

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hindering of internanoparticle interactions and possible plasticizing effect of the surfactant.53 The sharp diminution of the strain at break for the nanocomposite reinforced with 10 wt % M-CNC could be probably ascribed to aggregation occurring for such nanofiller contents. SEM can be used to reveal the microstructure of the material even if individual nanocrystals are not visible because of the nanoscale dimension of the reinforcing phase. This technique helps to conclude about the homogeneity of the composite, microscale dispersion of CNC within the continuous matrix, aggregation, sedimentation, and possible orientation of the nanorods. When observing the surface of the films (Figure S3), differences were observed between the nanocomposites reinforced with modified or nonmodified CNC. The PP matrix (Figure S3a) shows a smooth surface, whereas the nanocomposite reinforced with 3 wt % neat CNC (Figure S35b) displays a rougher surface and CNC aggregates are observed (circled in red). Improved dispersion is observed for M-CNC up to 6 wt % (Figure S3c−e), and nanocrystals seem to be homogeneously dispersed in the matrix. However, for the 10 wt % M-CNC reinforced PP composite film (Figure S3f), microscale nanoparticle aggregation is reported. The cryo-fractured cross section of the nanocomposite films was also investigated using SEM (Figure 10). By comparing Figure 10a (neat PP matrix) and Figure 10b (PP reinforced with 3 wt % unmodified CNC), the presence of the filler is evidenced through the observation of white dots probably corresponding to CNC aggregates. Moreover, some holes can be observed (circled in red) attributed to pulled-out CNC aggregates. Figures 10c−e (PP reinforced with up to 6 wt % CNC modified with quaternary ammonium salt) show similar appearance as neat PP matrix and absence of holes evidencing a homogeneous dispersion of CNC within the PP matrix. However, for 10 wt % M-CNC (Figure 10f) holes due to CNC aggregates are observed again (circled in red). Melt rheology experiments were conducted at 180 °C. The evolution of the storage modulus (G′), loss modulus (G″), and complex viscosity (η*) versus frequency was measured for CNC/M-CNC reinforced composites, and results are shown in Figure 11. By comparing the behavior of freshly melted PP and initially extruded PP (PPEx), a very slight decrease is observed after extrusion at low shear rates showing that the polymer is practically not degraded by the extrusion process. For nanocomposites, a clear decrease is reported, particularly at low shear rates, as the CNC content increases. The results are contrast with the usual predictions by Einstein54 and Batchelor55 for the relative viscosity increase of a suspension of particles with the volume fraction of suspended particles. This phenomenon has been reported for several nanoparticle-based systems56−62,43 and attributed to a dilution effect.

effect is reported, and the highest reinforcing effect is induced by 10 wt % M-CNC. However, this reinforcing effect should be taken with caution and, at least partially, attributed to the increase of the crystallinity of the PP matrix evidenced from DSC measurements. The nonlinear mechanical behavior of CNC-/M-CNCreinforced PP nanocomposites was characterized at room temperature. Figure 9 shows typical stress−strain curves, and

Figure 9. Typical stress−strain curves for neat extruded PP (●) and nanocomposites reinforced with 3 wt % CNC (open red circles) and 1 wt % (solid blue circles), 3 wt % (solid red circles), 6 wt % (solid green circles), and 10 wt % M-CNC (solid orange circles). The insert is an expanded view of stress vs strain curves for the low strain region.

the tensile data are reported in Table 3. Compared to that of the neat PP film, the modulus slightly increases, whereas the yield stress slightly decreases for nanocomposites films. However, the variation remains within the standard deviation. This can be an indication of weak compatibility and low stress transfer at the filler−matrix interface even in the case of compatibilized CNC. A more significant decrease of the yield strain is observed when adding cellulose nanomaterial, but the most important change is observed for the strain at break. It decreases when adding 3 wt % unmodified CNC but significantly increases for M-CNC, except for 10 wt %. The expected poor dispersion and distribution of unmodified CNC in the PP matrix caused brittle fracture of the composite as already reported for tunicin CNC51,52 and cellulose nanofibrils53 reinforced PP. The much higher strain at break values reported for M-CNC reinforced nanocomposites, even surpassing the strain at break for the neat PP matrix, is a good indication of the more homogeneous dispersion of the nanofiller within the PP matrix. Such behavior was already reported for tunicin CNC coated with phosphoric ester of polyoxyethylene (9) nonylphenyl ether51 and cellulose nanofibrils coated with of polyoxyethylene (10) nonylphenyl ether53 reinforced PP. The large plastic deformation of the material was attributed to the

Table 3. Young’s Modulus (E), Yield Stress (σy), Yield Strain (εy), and Strain at Break (εb) for Neat Extruded PP and Nanocomposites sample

E (MPa)

σy (MPa)

εy (%)

εb (%)


181 ± 67 321 ± 47 200 ± 19 231 ± 39 231 ± 55 279 ± 55

12.3 ± 2.1 10.3 ± 1.1 10.6 ± 1.5 11.0 ± 2.1 11.1 ± 1.3 9.16 ± 1.05

19.7 ± 3.4 13.7 ± 1.3 13.7 ± 1.9 12.8 ± 2.1 13.7 ± 1.6 7.70 ± 0.88

39.4 ± 6.2 15.4 ± 3.7 326 ± 18 109 ± 28 353 ± 23 12.0 ± 6.8


DOI: 10.1021/acsami.6b01650 ACS Appl. Mater. Interfaces XXXX, XXX, XXX−XXX

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Figure 10. SEM images of the cryo-fractured cross section of the extruded films: neat PP (a), and PP nanocomposites reinforced with 3 wt % unmodified CNC (b), and 1 wt % (c), 3 wt % (d), 6 wt % (e) and 10 wt % (f) CNC modified with quaternary ammonium salt.

Figure 11. Evolution of (a) the storage modulus (G′), (b) loss modulus (G″), and (c) complex viscosity (η*) vs of frequency for neat PP (○), neat extruded PP (●) and nanocomposites reinforced with 3 wt % CNC (open red circles) and 1 wt % (solid blue circles), 3 wt % (solid red circles), 6 wt % (solid green circles), and 10 wt % M-CNC (solid orange circles)


extraction step to establish favorable ionic interactions with quaternary ammonium salt bearing long alkyl chain. Hydrophobization of the CNC surface was verified by FTIR spectroscopy and contact angle measurements, and it was observed that modified CNC displays improved thermal stability

We have reported an environmentally friendly water-based, flexible, and easy procedure to modify the surface of CNC. It profitably uses the sulfate groups borne on the surface of CNC that are negatively charged and result from the sulfuric acid H

DOI: 10.1021/acsami.6b01650 ACS Appl. Mater. Interfaces XXXX, XXX, XXX−XXX

Research Article

ACS Applied Materials & Interfaces

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compared to that of neat CNC. Hydrophobized CNC disperses well in different nonpolar solvents and hydrophobic polymer matrix such as PP, which is impossible for neat CNC. Both unmodified and modified CNCs act as nucleating agents for the PP matrix, promoting its crystallization. A modest reinforcing effect was evidenced from DMA and tensile tests, but a spectacular improvement of the elongation at break was observed when adding a few percent of modified CNC. This large plastic deformation of the material was attributed to the hindering of internanoparticle interactions and possible plasticizing effect of the surfactant. A significant decrease of the melt viscosity was reported when adding CNC and ascribed to a dilution effect.


S Supporting Information *

The Supporting Information is available free of charge on the ACS Publications website at DOI: 10.1021/acsami.6b01650. UV transmittance spectra, DSC thermograms, and SEM images of the surface for PP and nanocomposites reinforced with unmodified CNC and modified CNC. (PDF)


Corresponding Author

*E-mail: [email protected]. Tel.: +33 476826995. Fax: +33 476826933. Address: The International School of Paper, Print Media and Biomaterials (Pagora), CS10065, 38402 Saint Martin d’Hères CEDEX, France. Notes

The authors declare no competing financial interest.

ACKNOWLEDGMENTS LGP2 and LRP are part of the LabEx Tec 21 (Investissements d’Avenir - grant agreement no. ANR-11-LABX-0030) and the PolyNat Carnot Institut (Investissements d’Avenir - grant agreement no. ANR-11-CARN-030-01).


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DOI: 10.1021/acsami.6b01650 ACS Appl. Mater. Interfaces XXXX, XXX, XXX−XXX

Research Article

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DOI: 10.1021/acsami.6b01650 ACS Appl. Mater. Interfaces XXXX, XXX, XXX−XXX